Zirconium-doped tantalum oxide films

ABSTRACT

Dielectric layers containing a zirconium-doped tantalum oxide layer, where the zirconium-doped tantalum oxide layer can be formed of one or more monolayers of tantalum oxide doped with zirconium, provide an insulating layer in a variety of structures for use in a wide range of electronic devices.

This application is a continuation of U.S. application Ser. No. 12/855,531, filed Aug. 12, 2010, which is a continuation of Ser. No. 11/608,281, filed Dec. 8, 2006, now issued as U.S. Pat. No. 7,776,762, which is a divisional of U.S. application Ser. No. 10/909,959 filed Aug. 2, 2004, now issued as U.S. Pat. No. 7,601,649, which applications are incorporated herein by reference in their entirety.

TECHNICAL FIELD

This application relates generally to semiconductor devices and device fabrication and, more particularly, to dielectric layers and their method of fabrication.

BACKGROUND

The semiconductor device industry has a market driven need to improve speed performance, improve its low static (off-state) power requirements, and lower production costs for its silicon based microelectronic products. In particular, there is continuous pressure to reduce the size of devices such as transistors. To reduce transistor size, the thickness of the silicon dioxide, SiO₂, gate dielectric is reduced in proportion to the shrinkage of the gate length. For example, a metal-oxide-semiconductor field effect transistor (MOSFET) would use a 1.5 nm thick SiO₂ gate dielectric for a gate length of 70 nm. The ultimate goal is to fabricate increasingly smaller and more reliable integrated circuits (ICs) for use in products such as processor chips, mobile telephones, and memory devices such as dynamic random access memories (DRAMs).

Currently, the semiconductor industry relies on the ability to reduce or scale the dimensions of its basic devices, primarily, the silicon based MOSFET. This device scaling includes scaling the gate dielectric, which has primarily been fabricated using silicon dioxide. A thermally grown amorphous SiO₂ layer provides device scaling includes scaling the gate dielectric, which has primarily been fabricated using silicon dioxide. A thermally grown amorphous SiO₂ layer provides an electrically and thermodynamically stable material, where the interface of the SiO₂ layer with underlying silicon provides a high quality interface as well as superior electrical isolation properties. However, increased scaling and other requirements in microelectronic devices have created the need to use other dielectric materials as gate dielectrics.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 depicts an atomic layer deposition system for fabricating a dielectric layer containing a zirconium-doped tantalum oxide, according to various embodiments of the present invention.

FIG. 2 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide, according to various embodiments of the present invention.

FIG. 3 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide, according to the present invention.

FIG. 4 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide, according to the present invention.

FIG. 5 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide including substituting a zirconium sequence for a tantalum sequence, according to the present invention.

FIG. 6 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide including commonly pulsing a zirconium precursor and a tantalum precursor, according to the present invention.

FIG. 7 shows an embodiment of a configuration of a transistor having a dielectric layer containing an atomic layer deposited zirconium-doped tantalum oxide, according to the present invention.

FIG. 8 shows an embodiment of a configuration of a transistor with a floating gate having a dielectric layer containing an atomic layer deposited zirconium-doped tantalum oxide, according to the present invention.

FIG. 9 shows an embodiment of a configuration of a capacitor having a dielectric layer containing an atomic layer deposited zirconium-doped tantalum oxide, according to the present invention.

FIG. 10 depicts an embodiment of a dielectric layer including a nanolaminate having at least one layer containing an atomic layer deposited zirconium-doped tantalum oxide, according to the present invention.

FIG. 11 is a simplified diagram for an embodiment of a controller coupled to an electronic device, according to the present invention.

FIG. 12 illustrates a diagram for an embodiment of an electronic system having devices with a dielectric film containing an atomic layer deposited zirconium-doped tantalum oxide, according to the present invention.

DETAILED DESCRIPTION

The following detailed description refers to the accompanying drawings that show, by way of illustration, specific aspects and embodiments in which the present invention may be practiced. These embodiments are described in sufficient detail to enable those skilled in the art to practice the present invention. Other embodiments may be utilized and structural, logical, and electrical changes may be made without departing from the scope of the present invention. The various embodiments disclosed herein are not necessarily mutually exclusive, as some disclosed embodiments can be combined with one or more other disclosed embodiments to form new embodiments.

The terms wafer and substrate used in the following description include any structure having an exposed surface with which to form an integrated circuit (IC) structure. The term substrate is understood to include semiconductor wafers. The term substrate is also used to refer to semiconductor structures during processing, and may include other layers that have been fabricated thereupon. Both wafer and substrate include doped and undoped semiconductors, epitaxial semiconductor layers supported by a base semiconductor or insulator, as well as other semiconductor structures well known to one skilled in the art. The term conductor is understood to generally include n-type and p-type semiconductors and the term insulator or dielectric is defined to include any material that is less electrically conductive than the materials referred to as conductors or as semiconductors.

The term “horizontal” as used in this application is defined as a plane parallel to the conventional plane or surface of a wafer or substrate, regardless of the orientation of the wafer or substrate. The term “vertical” refers to a direction perpendicular to the horizontal as defined above. Prepositions, such as “on”, “side” (as in “sidewall”), “higher”, “lower”, “over” and “under” are defined with respect to the conventional plane or surface being on the top surface of the wafer or substrate, regardless of the orientation of the wafer or substrate. The following detailed description is, therefore, not to be taken in a limiting sense, and the scope of the present invention is defined only by the appended claims, along with the full scope of equivalents to which such claims are entitled.

A gate dielectric in a transistor has both a physical gate dielectric thickness and an equivalent oxide thickness (t_(eq)). The equivalent oxide thickness quantifies the electrical properties, such as capacitance, of the gate dielectric in terms of a representative physical thickness. t_(eq) is defined as the thickness of a theoretical SiO₂ layer that would be required to have the same capacitance density as a given dielectric, ignoring leakage current and reliability considerations.

A SiO₂ layer of thickness, t, deposited on a Si surface as a gate dielectric will have a t_(eq) larger than its thickness, t. This t_(eq) results from the capacitance in the surface channel on which the SiO₂ is deposited due to the formation of a depletion/inversion region. This depletion/inversion region can result in t_(eq) being from 3 to 6 Angstroms (Å) larger than the SiO₂ thickness, t. Thus, with the semiconductor industry driving to someday scale the gate dielectric equivalent oxide thickness to under 10 Å, the physical thickness requirement for a SiO₂ layer used for a gate dielectric would be need to be approximately 4 to 7 Å.

Additional requirements on a SiO₂ layer would depend on the gate electrode used in conjunction with the SiO₂ gate dielectric. Using a conventional polysilicon gate would result in an additional increase in t_(eq) for the SiO₂ layer. This additional thickness could be eliminated by using a metal gate electrode, though metal gates are not currently used in typical complementary metal-oxide-semiconductor field effect transistor (CMOS) technology. Thus, future devices would be designed towards a physical SiO₂ gate dielectric layer of about 5 Å or less. Such a small thickness requirement for a SiO₂ oxide layer creates additional problems.

Silicon dioxide is used as a gate dielectric, in part, due to its electrical isolation properties in a SiO₂—Si based structure. This electrical isolation is due to the relatively large band gap of SiO₂ (8.9 eV) making it a good insulator from electrical conduction. Signification reductions in its band gap would eliminate it as a material for a gate dielectric. As the thickness of a SiO₂ layer decreases, the number of atomic layers, or monolayers of the material in the thickness decreases. At a certain thickness, the number of monolayers will be sufficiently small that the SiO₂ layer will not have a complete arrangement of atoms as in a larger or bulk layer. As a result of incomplete formation relative to a bulk structure, a thin SiO₂ layer of only one or two monolayers will not form a full band gap. The lack of a full band gap in a SiO₂ gate dielectric would cause an effective short between an underlying Si channel and an overlying polysilicon gate. This undesirable property sets a limit on the physical thickness to which a SiO₂ layer can be scaled. The minimum thickness due to this monolayer effect is thought to be about 7-8 Å.

Therefore, for future devices to have a t_(eq) less than about 10 Å, other dielectrics than SiO₂ need to be considered for use as a gate dielectric.

For a typical dielectric layer used as a gate dielectric, the capacitance is determined as one for a parallel plate capacitance: C=κε₀A/t, where κ is the dielectric constant, ε₀ is the permittivity of free space, A is the area of the capacitor, and t is the thickness of the dielectric. The thickness, t, of a material is related to its t_(eq) for a given capacitance, with SiO₂ having a dielectric constant κ_(ox)=3.9, as

t=(κ/κ_(ox)) t _(eq)=(κ/3.9) t _(eq).

Thus, materials with a dielectric constant greater than that of SiO₂, 3.9, will have a physical thickness that can be considerably larger than a desired t_(eq), while providing the desired equivalent oxide thickness. For example, an alternate dielectric material with a dielectric constant of 10 could have a thickness of about 25.6 Å to provide a t_(eq) of 10 Å, not including any depletion/inversion layer effects. Thus, a reduced equivalent oxide thickness for transistors can be realized by using dielectric materials with higher dielectric constants than SiO₂.

The thinner equivalent oxide thickness required for lower transistor operating voltages and smaller transistor dimensions may be realized by a significant number of materials, but additional fabricating requirements makes determining a suitable replacement for SiO₂ difficult. The current view for the microelectronics industry is still for Si based devices. This requires that the gate dielectric employed be grown on a silicon substrate or silicon layer, which places significant constraints on the substitute dielectric material. During the formation of the dielectric on the silicon layer, there exists the possibility that a small layer of SiO₂ could be formed in addition to the desired dielectric. The result would effectively be a dielectric layer consisting of two sublayers in parallel with each other and the silicon layer on which the dielectric is formed. In such a case, the resulting capacitance would be that of two dielectrics in series. As a result, the t_(eq) of the dielectric layer would be the sum of the SiO₂ thickness and a multiplicative factor of the thickness, t, of the dielectric being formed, written as

t _(eq) =t _(SiO2)+(κ_(ox)/κ)t.

Thus, if a SiO₂ layer is formed in the process, the t_(eq) is again limited by a SiO₂ layer. In the event that a barrier layer is formed between the silicon layer and the desired dielectric in which the barrier layer prevents the formation of a SiO₂ layer, the t_(eq) would be limited by the layer with the lowest dielectric constant. However, whether a single dielectric layer with a high dielectric constant or a barrier layer with a higher dielectric constant than SiO₂ is employed, the layer interfacing with the silicon layer must provide a high quality interface to maintain a high channel carrier mobility.

One of the advantages using SiO₂ as a gate dielectric has been that the formation of the SiO₂ layer results in an amorphous gate dielectric. Having an amorphous structure for a gate dielectric provides for reducing problems of leakage current associated with grain boundaries in polycrystalline gate dielectrics that provide high leakage paths. Additionally, grain size and orientation changes throughout a polycrystalline gate dielectric can cause variations in the film's dielectric constant, along with uniformity and surface topography problems. Typically, materials having the advantage of a high dielectric constant relative to SiO₂ also have the disadvantage of a crystalline form, at least in a bulk configuration. The best candidates for replacing SiO₂ as a gate dielectric are those with high dielectric constant, which can be fabricated as a thin layer with an amorphous form.

High-κ materials include materials having a dielectric constant greater than silicon dioxide, for example, dielectrics materials having a dielectric constant greater than about twice the dielectric constant of silicon dioxide. By introducing a dopant into a high-κ metal oxide dielectric, its amorphous-to-polycrystalline temperature can be increased. The dopant acts to disturb the ordered structure of the original film. Elements usable as dopants in some high-κ materials have include Si, Al, Zr, Hf, and N. By adjusting the amount of the dopants in the original film, the physical and electrical properties of such metal oxides may be tailored. Bulk (Ta₂O₅)_(1-x)(Zr₂O)_(x) polycrystalline ceramics, formed by mixing powders of Ta₂O₅ and Zr₂O and sintering at high temperatures, have increased dielectric constants with respect to Ta₂O₅ for certain amounts of Zr in the bulk (Ta₂O₅)_(1-x)(Zr₂O)_(x) structure.

An appropriate high-K gate dielectric should have a large energy gap (E_(g)) and large energy barrier heights with Si for both electrons and holes. Generally, the bandgap is inversely related to the dielectric constant for a high-κ material, which lessens some advantages of the high-κ material. Tantalum oxide (Ta₂O₅) is a potential replacement for SiO₂. It has a bandgap of about 4.5 eV and a dielectric constant of about 26. Further, Ta₂O₅ is a suitable candidate for engineering its physical and electrical properties by doping, since its structure does not change significantly with the addition of a substantial amount of another oxide. However, forming Ta₂O₅ on a silicon substrate may result in an interface layer that contains SiO₂, in particular at processing temperatures above 700° C. The material composition and its properties of an interface layer are typically dependent on process conditions and the condition of the substrate before forming the dielectric layer. Though the existence of an interface layer may effectively reduce the dielectric constant associated with the dielectric layer and its substrate interface layer, a SiO₂ interface layer or other composition interface layer, may improve the interface density, fixed charge density, and channel mobility of a device having this interface layer.

An embodiment for a method for forming a dielectric layer includes forming a dielectric film containing a zirconium-doped tantalum oxide by depositing tantalum on a substrate surface by atomic layer deposition and by depositing zirconium by atomic layer deposition on the substrate surface. Embodiments include structures for capacitors, transistors, memory devices, and electronic systems with dielectric layers containing atomic layer deposited zirconium-doped tantalum oxide, and methods for forming such structures.

Embodiments for forming a tantalum oxide layer, or film, by atomic layer deposition include doping the tantalum oxide with zirconium. An undoped tantalum oxide film may be a film having a specific stoichiometry such as Ta₂O₅ or it may be a non-stoichiometric tantalum oxide, Ta_(y)O_(x), which is represented herein as TaO_(x). The zirconium doping may be performed as a doping by zirconium atoms or by zirconium oxide ZrO_(x), where x may be x=2. The resulting film may be considered TaO_(x) doped with Zr or ZrO_(x).

Embodiments of dielectric layers containing an atomic layer deposited zirconium-doped tantalum oxide layer have a larger dielectric constant than silicon dioxide. Such dielectric layers provide a significantly thinner equivalent oxide thickness compared with a silicon oxide layer having the same physical thickness. Alternately, such dielectric layers provide a significantly thicker physical thickness than a silicon oxide layer having the same equivalent oxide thickness. This increased physical thickness aids in reducing leakage current.

Another consideration for selecting the material and method for forming a dielectric film for use in electronic devices and systems concerns the roughness of a dielectric film on a substrate. Surface roughness of the dielectric film has a significant effect on the electrical properties of the gate oxide, and the resulting operating characteristics of the transistor. The leakage current through a physical 1.0 nm gate oxide increases by a factor of 10 for every 0.1 increase in the root-mean-square (RMS) roughness.

During a conventional sputtering deposition process stage, particles of the material to be deposited bombard the surface at a high energy. When a particle hits the surface, some particles adhere, and other particles cause damage. High energy impacts remove body region particles creating pits. The surface of such a deposited layer can have a rough contour due to the rough interface at the body region.

In an embodiment, a zirconium-doped tantalum oxide dielectric film having a substantially smooth surface relative to other processing techniques is formed using atomic layer deposition (ALD). Further, forming such a dielectric film using atomic layer deposition can provide for controlling transitions between material layers. Thus, atomic layer deposited zirconium-doped tantalum oxide dielectric films can have an engineered transition with a substrate surface.

ALD, also known as atomic layer epitaxy (ALE), is a modification of chemical vapor deposition (CVD) and is also called “alternatively pulsed-CVD.” In ALD, gaseous precursors are introduced one at a time to the substrate surface mounted within a reaction chamber (or reactor). This introduction of the gaseous precursors takes the form of pulses of each gaseous precursor. In a pulse of a precursor gas, the precursor gas is made to flow into a specific area or region for a short period of time. Between the pulses, the reaction chamber is purged with a gas, which in many cases is an inert gas, and/or evacuated.

In a chemisorption-saturated ALD (CS-ALD) process, during the first pulsing phase, reaction with the substrate occurs with the precursor saturatively chemisorbed at the substrate surface. Subsequent pulsing with a purging gas removes precursor excess from the reaction chamber.

The second pulsing phase introduces another precursor on the substrate where the growth reaction of the desired film takes place. Subsequent to the film growth reaction, reaction byproducts and precursor excess are purged from the reaction chamber. With favourable precursor chemistry where the precursors adsorb and react with each other on the substrate aggressively, one ALD cycle can be preformed in less than one second in properly designed flow type reaction chambers. Typically, precursor pulse times range from about 0.5 sec to about 2 to 3 seconds.

In ALD, the saturation of all the reaction and purging phases makes the growth self-limiting. This self-limiting growth results in large area uniformity and conformality, which has important applications for such cases as planar substrates, deep trenches, and in the processing of porous silicon and high surface area silica and alumina powders. Significantly, ALD provides for controlling film thickness in a straightforward manner by controlling the number of growth cycles.

ALD was originally developed to manufacture luminescent and dielectric films needed in electroluminescent displays. Significant efforts have been made to apply ALD to the growth of doped zinc sulfide and alkaline earth metal sulfide films. Additionally, ALD has been studied for the growth of different epitaxial II-V and II-VI films, nonepitaxial crystalline or amorphous oxide and nitride films and multilayer structures of these. There also has been considerable interest towards the ALD growth of silicon and germanium films, but due to the difficult precursor chemistry, this has not been very successful.

The precursors used in an ALD process may be gaseous, liquid or solid. However, liquid or solid precursors should be volatile. The vapor pressure should be high enough for effective mass transportation. Also, solid and some liquid precursors may need to be heated inside the reaction chamber and introduced through heated tubes to the substrates. The necessary vapor pressure should be reached at a temperature below the substrate temperature to avoid the condensation of the precursors on the substrate. Due to the self-limiting growth mechanisms of ALD, relatively low vapor pressure solid precursors can be used though evaporation rates may somewhat vary during the process because of changes in their surface area.

There are several other requirements for precursors used in ALD. The precursors should be thermally stable at the substrate temperature because their decomposition would destroy the surface control and accordingly the advantages of the ALD method which relies on the reaction of the precursor at the substrate surface. A slight decomposition, if slow compared to the ALD growth, can be tolerated.

The precursors should chemisorb on or react with the surface, though the interaction between the precursor and the surface as well as the mechanism for the adsorption is different for different precursors. The molecules at the substrate surface should react aggressively with the second precursor to form the desired solid film. Additionally, precursors should not react with the film to cause etching, and precursors should not dissolve in the film. Using highly reactive precursors in ALD contrasts with the selection of precursors for conventional CVD.

The by-products in the reaction should be gaseous in order to allow their easy removal from the reaction chamber. Further, the by-products should not react or adsorb on the surface.

In a reaction sequence ALD (RS-ALD) process, the self-limiting process sequence involves sequential surface chemical reactions. RS-ALD relies on chemistry between a reactive surface and a reactive molecular precursor. In an RS-ALD process, molecular precursors are pulsed into the ALD reaction chamber separately. The metal precursor reaction at the substrate is typically followed by an inert gas pulse to remove excess precursor and by-products from the reaction chamber prior to pulsing the next precursor of the fabrication sequence.

By RS-ALD, films can be layered in equal metered sequences that are all identical in chemical kinetics, deposition per cycle, composition, and thickness. RS-ALD sequences generally deposit less than a full layer per cycle. Typically, a deposition or growth rate of about 0.25 to about 2.00 Å per RS-ALD cycle can be realized.

The advantages of RS-ALD include continuity at an interface avoiding poorly defined nucleating regions that are typical for chemical vapor deposition (<20 Å) and physical vapor deposition (<50 Å), conformality over a variety of substrate topologies, use of low temperature and mildly oxidizing processes, lack of dependence on the reaction chamber, growth thickness dependent solely on the number of cycles performed, and ability to engineer multilayer laminate films with resolution of one to two monolayers. RS-ALD processes RS-ALD allows for deposition control on the order on monolayers and the ability to deposit monolayers of amorphous films.

Herein, a sequence refers to the ALD material formation based on an ALD reaction of one precursor with its reactant precursor. For example, forming tantalum oxide from a TaI₄ precursor and H₂O₂, as its reactant precursor, forms an embodiment of a tantalum/oxygen sequence, which can also be referred to as tantalum sequence. A cycle of a sequence includes pulsing a precursor, pulsing a purging gas for the precursor, pulsing a reactant precursor, and pulsing the reactant's purging gas.

In an embodiment, a layer of zirconium-doped TaO_(x) is formed on a substrate mounted in a reaction chamber using ALD in a repetitive sequence using precursor gases individually pulsed into the reaction chamber. Alternately, solid or liquid precursors can be used in an appropriately designed reaction chamber.

FIG. 1 shows an embodiment of an atomic layer deposition system 100 for processing a dielectric film containing zirconium-doped tantalum oxide. The elements depicted permit discussion of the present invention such that those skilled in the art may practice the present invention without undue experimentation. In FIG. 1, a substrate 110 is located inside a reaction chamber 120 of ALD system 100. Also located within the reaction chamber 120 is a heating element 130 which is thermally coupled to substrate 110 to control the substrate temperature. A gas-distribution fixture 140 introduces precursor gases to the substrate 110. Each precursor gas originates from individual gas sources 151-154 whose flow is controlled by mass-flow controllers 156-159, respectively. Gas sources 151-154 provide a precursor gas either by storing the precursor as a gas or by providing a location and apparatus for evaporating a solid or liquid material to form the selected precursor gas.

Also included in the ALD system are purging gas sources 161, 162, each of which is coupled to mass-flow controllers 166, 167, respectively. Furthermore, additional purging gas sources can be constructed in ALD system 100, one purging gas source for each precursor gas, for example. For a process that uses the same purging gas for multiple precursor gases less purging gas sources are required for ALD system 100. Gas sources 151-154 and purging gas sources 161-162 are coupled by their associated mass-flow controllers to a common gas line or conduit 170 which is coupled to the gas-distribution fixture 140 inside the reaction chamber 120. Gas conduit 170 is also coupled to vacuum pump, or exhaust pump, 181 by mass-flow controller 186 to remove excess precursor gases, purging gases, and by-product gases at the end of a purging sequence from the gas conduit.

Vacuum pump, or exhaust pump, 182 is coupled by mass-flow controller 187 to remove excess precursor gases, purging gases, and by-product gases at the end of a purging sequence from reaction chamber 120. For convenience, control displays, mounting apparatus, temperature sensing devices, substrate maneuvering apparatus, and necessary electrical connections as are known to those skilled in the art are not shown in FIG. 1. Though ALD system 100 is well suited for practicing the present invention, other ALD systems commercially available can be used.

The use, construction and fundamental operation of reaction chambers for deposition of films are understood by those of ordinary skill in the art of semiconductor fabrication. The present invention man be practiced on a variety of such reaction chambers without undue experimentation. Furthermore, one of ordinary skill in the art will comprehend the necessary detection, measurement, and control techniques in the art of semiconductor fabrication upon reading the disclosure.

The elements of ALD system 100 can be controlled by a computer. To focus on the use of ALD system 100 in the various embodiments of the present invention, the computer is not shown. Those skilled in the art can appreciate that the individual elements such as pressure control, temperature control, and gas flow within ALD system 100 can be under computer control.

FIG. 2 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide. At 210, tantalum is deposited onto a substrate surface by atomic layer deposition. A number of precursors containing tantalum may be used to deposit the tantalum. In addition, the pulsing of the tantalum precursor may use a pulsing period that provides uniform coverage of a monolayer on the surface or may use a pulsing period that provides partial formation of a monolayer on the surface. At 220, zirconium is deposited by atomic layer deposition on the substrate surface. A reaction precursor may be pulsed after each pulsing of the tantalum precursor to form TaO_(x) and another reaction precursor may be pulsed after each pulsing of the zirconium precursor to dope the TaO_(x) with ZrO_(x). The two reaction precursors may have a common composition. In an embodiment, to provide zirconium atom doping, deposition of the zirconium is not followed by a reaction precursor but by another pulsing of the tantalum precursor. Alternately, a reaction precursor to provide an oxidizing precursor may be pulsed after tantalum and zirconium have deposited. Appropriate purging pulses are performed between the pulsing of each element bearing precursor and each reaction precursor. The pulsing of the tantalum and zirconium precursors may be regulated to provide a selected ratio of zirconium atoms to the sum of tantalum and zirconium atoms to provide a desired doping.

FIG. 3 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide. At 310, a tantalum containing precursor is pulsed to deposit tantalum onto a substrate surface. A number of precursors containing tantalum may be used to deposit the tantalum. At 320, an oxygen containing precursor is pulsed to deposit oxygen on the substrate surface. A number of precursors containing oxygen may be used to deposit the oxygen. The tantalum on the substrate surface and the oxygen react to form one or more monolayers or a portion of a monolayer of TaO_(x). Precursors may be used that contain tantalum and oxygen such that TaO_(x) is deposited on the substrate surface in a single pulsing. Appropriate purging pulses may be generated between the pulsing of the tantalum bearing precursor and the pulsing of the oxygen bearing precursor. At 330, a number of cycles of the pulsing of the tantalum containing precursor and the pulsing of the oxygen containing precursor is repeated. The number of cycles depends on the monolayer coverage desired and the desired amount of the tantalum to be contained in the doped TaO_(x) being processed. At 340, a zirconium cycle is substituted for one or more cycles of the pulsing of the tantalum containing precursor, where the zirconium containing precursor deposits zirconium onto the substrate surface. A number of precursors containing zirconium and a number of precursors containing oxygen may be used to deposit ZrO_(x) as the dopant for the TaO_(x) film being formed. Cycles using a number of precursors containing zirconium without an oxidizing reaction precursor may be used to deposit Zr as the dopant for the TaO_(x) film being formed.

In the embodiment of FIG. 3, to provide the zirconium dopant into the TaO_(x) film, a variation to the repeated cycles may be made. The doping is included in the atomic layer deposition process by pulsing a zirconium containing precursor and reactant precursor in place of one or more cycles of the tantalum sequence. Associated with the dopant cycle there is also a growth rate substantially constant at a fixed number of angstroms per cycle, for constant environmental conditions in the reaction chamber and constant sequencing parameters in the dopant cycle. However, when a combined cycle consists of a large number of cycles of a tantalum sequence for one cycle of a zirconium dopant cycle, the growth rate for forming the zirconium-doped TaO_(x) dielectric film may be substantially the same as for an undoped TaO_(x) dielectric film. When the number of cycles for a zirconium dopant sequence is no longer small with respect to the number of cycles for a tantalum sequence, growth rates can vary from that of an undoped TaO_(x) dielectric film. As can be understood by those skilled in the art, particular growth rates can be determined during normal initial testing of the ALD system for processing a zirconium-doped TaO_(x) dielectric film for a given application without undue experimentation.

FIG. 4 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide. At 410, a tantalum containing precursor is pulsed to deposit tantalum onto a substrate surface. A number of precursors containing tantalum may be used to deposit the tantalum. At 420, a zirconium containing precursor is pulsed to deposit zirconium by atomic layer deposition. The zirconium containing precursor is pulsed during a portion of the time that the tantalum containing precursor is being pulsed. A number of precursors containing zirconium may be used to deposit the zirconium. At 430, a reaction precursor is pulsed. The reaction precursor provides an oxidizing reaction at the substrate surface to form TaO_(x) doped with zirconium. The zirconium dopant may be ZrO_(x).

In the embodiment of FIG. 4, the zirconium containing precursor can be pulsed simultaneously with the tantalum containing precursor. Then, following a gas purge, a reactant precursor that provides an ALD reaction for both the tantalum containing precursor and the zirconium precursor is pulsed into the reaction. The percentage of the zirconium can be controlled by regulating the percentage of the zirconium containing precursor in the precursor mixture that is injected into the reaction chamber to the substrate. The growth per cycle would then depend on the growth rate using the given mixture. As can be understood by those skilled in the art, determining the growth rate for a particular mixture can be determined during normal initial testing of the ALD system for processing a zirconium-doped TaO_(x) dielectric film without undue experimentation.

Atomic layer deposition of the individual components of the zirconium-doped TaO_(x) layer allows for individual control of each precursor pulsed into the reaction chamber. Thus, each precursor is pulsed into the reaction chamber for a predetermined period, where the predetermined period can be set separately for each precursor. Additionally, for various embodiments for ALD formation of a zirconium-doped TaO_(x) layer, each precursor can be pulsed into the reaction under separate environmental conditions. The substrate can be maintained at a selected temperature and the reaction chamber maintained at a selected pressure independently for pulsing each precursor. Appropriate temperatures and pressures may be maintained, whether the precursor is a single precursor or a mixture of precursors. During atomic layer deposition, the pulsing of the precursor gases is separated by purging the reaction chamber with a purging gas following each pulsing of a precursor. In an embodiment, nitrogen gas is used as the purging gas following the pulsing of each precursor used in a cycle to form a film of zirconium-doped TaO_(x). Additionally, the reaction chamber can also be purged by evacuating the reaction chamber.

FIG. 5 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide including substituting a zirconium sequence for a tantalum sequence. This embodiment can be implemented with the atomic layer deposition system 100 of FIG. 1. At 505, a substrate 110 is prepared. The substrate used for forming a transistor is typically a silicon or silicon containing material. In other embodiments, germanium, gallium arsenide, silicon-on-sapphire substrates, or other suitable substrates may be used. This preparation process includes cleaning substrate 110 and forming layers and regions of the substrate, such as drains and sources of a metal oxide semiconductor (MOS) transistor, prior to forming a gate dielectric. In an embodiment, the substrate is cleaned to provide an initial substrate depleted of its native oxide. In an embodiment, the initial substrate is cleaned to also provide a hydrogen-terminated surface. In an embodiment, a silicon substrate undergoes a final HF rinse prior to ALD processing to provide the silicon substrate with a hydrogen-terminated surface without a native silicon oxide layer.

The sequencing of the formation of the regions of the transistor being processed follows typical sequencing that is generally performed in the fabrication of a MOS transistor as is well known to those skilled in the art. Included in the processing prior to forming a gate dielectric is the masking of substrate regions to be protected during the gate dielectric formation, as is typically performed in MOS fabrication. In this embodiment, the unmasked region includes a body region of a transistor, however one skilled in the art will recognize that other semiconductor device structures may utilize this process. Additionally, the substrate 110 in its ready for processing form is conveyed into a position in reaction chamber 120 for ALD processing.

At 510, a tantalum containing precursor is pulsed into reaction chamber 120. In an embodiment, Ta(OC₂H₅)₅ is used as a precursor. The Ta(OC₂H₅)₅ is pulsed into reaction chamber 120 through the gas-distribution fixture 140 onto substrate 110. The flow of the Ta(OC₂H₅)₅ is controlled by mass-flow controller 156 from gas source 151, where the Ta(OC₂H₅)₅ is maintained at about 105° C. The pressure in reaction chamber is at about 10 mbar nitrogen pressure. In another embodiment, the substrate temperature is maintained between about 250° C. and about 325° C. by heating element 130. The upper bound of 325° C. is the highest temperature for Ta₂O₅ to form in the self-controlled growth regime. The Ta(OC₂H₅)₅ reacts with the surface of the substrate 110 in the desired region defined by the unmasked areas of the substrate 110. In other embodiments, a tantalum containing precursor includes TaCl₅.

At 515, a first purging gas is pulsed into the reaction chamber 120. In particular, nitrogen is used as a purging gas and a carrier gas. The nitrogen flow is controlled by mass-flow controller 166 from the purging gas source 161 into the gas conduit 170. Using the pure nitrogen purge avoids overlap of the precursor pulses and possible gas phase reactions. Following the purge, an oxygen containing precursor is pulsed into the reaction chamber 120, at 520.

For the tantalum sequence using a Ta(OC₂H₅)₅ or TaCl₅ as the precursor, water vapor is selected as the precursor acting as a reactant to form TaO_(x) on the substrate 110. The H₂O vapor is pulsed into the reaction chamber 120 through gas conduit 170 from gas source 152 by mass-flow controller 157. The water vapor aggressively reacts at the surface of substrate 110.

Following the pulsing of an oxygen containing precursor, a second purging gas is injected into the reaction chamber 120, at 525. Nitrogen gas is used to purge the reaction chamber after pulsing each precursor gas in the tantalum/oxygen sequence. Excess precursor gas, and reaction by-products are removed from the system by the purge gas in conjunction with the exhausting of the reaction chamber 120 using vacuum pump 182 through mass-flow controller 187, and exhausting of the gas conduit 170 by the vacuum pump 181 through mass-flow controller 186.

At 530, the pulsing of the tantalum containing precursor, the pulsing of the oxygen containing precursor, and the pulsing of the first and second purging gas are repeated for a number of cycles. After repeating the tantalum/oxygen sequence for a selected number of cycles, a zirconium containing precursor is pulsed into the reaction chamber 120, at 535.

In an embodiment, ZrI₄ is used as the zirconium containing precursor. Alternately, ZrCl₄ may be used as the zirconium containing precursor. The ZrI₄ precursor having a purity of about 99.5% or greater is evaporated from a containment area held at about 240° C. in gas source 152. Mass-flow controller 158 regulates the pulsing of the ZrI₄ precursor to the surface of the substrate 110 through gas-distribution fixture 140 from gas source 152. In an embodiment, the substrate temperature is maintained between about 230° C. and about 500° C. by heating element 130.

At 540, a third purging gas is introduced into the system. Nitrogen gas can also be used as a purging and carrier gas. The nitrogen flow is controlled by mass-flow controller 167 from the purging gas source 162 into the gas conduit 170 and subsequently into the reaction chamber 120. In another embodiment, argon gas is used as the purging gas. Following the pulsing of the third purging gas, a reactant precursor is pulsed into the reaction chamber 120, at 545. The reactant precursor is selected to produce an oxidizing reaction for the zirconium at the substrate surface. In an embodiment, the reactant precursor is H₂O—H₂O₂ vapor. Mass-flow controller 159 regulates the H₂O—H₂O₂ vapor pulsing into reaction chamber 120 through gas conduit 170 from gas source 153. The H₂O—H₂O₂ vapor aggressively reacts at the surface of substrate 110.

Following the pulsing of the reactant precursor, a fourth purging gas is injected into reaction chamber 120, at 550. Nitrogen gas may be used to purge the reaction chamber after pulsing each precursor gas in the zirconium/oxygen sequence. In another embodiment, argon gas may be used as the purging gas. Excess precursor gas, and reaction by-products are removed from the system by the purge gas in conjunction with the exhausting of reaction chamber 120 using vacuum pump 182 through mass-flow controller 187, and exhausting of the gas conduit 170 by the vacuum pump 181 through mass-flow controller 186.

During a ZrI₄/H₂O—H₂O₂ vapor sequence, the substrate is held between about 230° C. and about 500° C. by the heating element 130 with reaction chamber 120 held at about 250 Pa. In an embodiment, the ZrI₄ pulse time is about 2.0 sec. After the ZrI₄ pulse, the zirconium sequence continues with a purge pulse followed by a H₂O—H₂O₂ vapor pulse followed by a purge pulse. In an embodiment, the H₂O—H₂O₂ vapor pulse time is about 2.0 sec, and the ZrI₄ and the H₂O—H₂O₂ vapor purging pulse times are each at about 2.0 sec.

At 555, a determination is made as to whether the number of substituted zirconium cycles has equaled a predetermined number. The predetermined number of substitution cycles is selected to set the percentage of zirconium dopant in the TaO_(x) film. In an embodiment, the percentage is set ranging from about 5% to about 40% zirconium in the zirconium-doped TaO_(x) film with respect to an atomic ratio of zirconium atoms to the sum of zirconium and tantalum atoms. If the number of completed substitution cycles is less than the predetermined number, the zirconium containing precursor is pulsed into the reaction chamber, at 535, and the process continues. If the number of completed substitution cycles equals the predetermined number, then a determination is made as to whether a total number of combined cycles has been completed to form a desired thickness, at 560. If the total number of cycles to form the desired thickness has not been completed, a number of cycles for the tantalum/oxygen sequence is repeated, at 530, and the process continues. If the total number of cycles to form the desired thickness has been completed, the dielectric film containing zirconium-doped TaO_(x) may optionally be annealed. The zirconium-doped TaO_(x) film processed at these relatively low temperatures may provide an amorphous layer.

The thickness of a zirconium-doped TaO_(x) film is determined by a fixed growth rate for the pulsing periods and precursors used, set at a value such as N nm/combined cycle, dependent upon the number of cycles of the zirconium sequence relative to the tantalum sequence that form a combined sequence. For a desired zirconium-doped TaO_(x) film thickness, t, in an application such as forming a gate dielectric of a MOS transistor, the ALD process is repeated for t/N total combined cycles. Once the t/N cycles have completed, no further ALD processing for zirconium-doped TaO_(x) is required.

In various embodiments, the presence of residual chlorine in a zirconium-doped TaO_(x) dielectric film may be reduced or eliminated providing a substantially chlorine free film by using metal precursors other than metal chlorides in the ALD processing of each metal, tantalum and zirconium. Use of a metal iodine as a precursor results in a film substantially free of residual iodine. As a result, metal halide precursors other than chloride metal precursors may be used. Eliminating residual chloride in such dielectric films may provide reduced leakage current for devices having these dielectric films.

At 570, after forming the zirconium-doped TaO_(x), processing the device having the dielectric layer containing zirconium-doped TaO_(x) is completed. In an embodiment, completing the device includes completing the formation of a transistor. In another embodiment, completing the device includes completing the formation of a capacitor. Alternately, completing the process includes completing the construction of a memory device having an array with access transistors formed with gate dielectrics containing atomic layer deposited zirconium-doped TaO_(x). Further, in another embodiment, completing the process includes the formation of an electronic system including an information handling device that uses electronic devices with transistors formed with dielectric films containing atomic layer deposited zirconium-doped TaO_(x). Typically, information handling devices such as computers include many memory devices, having many access transistors.

It can appreciated by those skilled in the art that the elements of a method for forming an atomic layer deposited zirconium-doped TaO_(x) film in the embodiment of FIG. 5 can be performed with various number of cycles for the tantalum sequence and various number of cycles for the zirconium dopant sequence. In an embodiment, substituting a zirconium cycle for one or more cycles includes substituting a number of zirconium cycles to form a dielectric layer containing TaO_(x) doped with a predetermined percentage (atomic ratio) for the zirconium ranging from about 5% to about 40% zirconium. In another embodiment, the ALD processing of a zirconium-doped TaO_(x) dielectric film may provide a dielectric film having a dielectric constant ranging from about 8 to about 27 depending upon the existence of an interface layer at the surface of the silicon surface.

FIG. 6 illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a zirconium-doped tantalum oxide including commonly pulsing a zirconium precursor and a tantalum precursor. This embodiment can be implemented with the atomic layer deposition system 100 of FIG. 1. At 605, a substrate 110 is prepared in a similar manner has at 505 in FIG. 5. Then, a tantalum containing precursor is pulsed into reaction chamber 120, at 610. A zirconium containing precursor is pulsed into reaction chamber 120 substantially simultaneously with the pulsing of the tantalum containing precursor, at 615. Though the zirconium containing precursor is pulsed with the tantalum precursor, the period for the zirconium containing precursor may be less than the period for the tantalum containing precursor. The mixture of the zirconium containing precursor and the tantalum containing precursor is regulated such that the zirconium acts as a dopant in a dielectric film containing the tantalum. After pulsing the tantalum containing precursor and the zirconium containing precursor, a first purging gas is pulsed into reaction chamber 120, at 620. Excess precursor gases and reaction by-products are removed from the system by the purge gas in conjunction with the exhausting of the reaction chamber 120 using vacuum pump 182 through mass-flow controller 187, and exhausting of the gas conduit 170 by the vacuum pump 181 through mass-flow controller 186.

A reactant containing precursor is pulsed into reaction chamber 120, at 625. The reactant containing precursor provides an oxidizing reaction at substrate 110. A second purging gas is pulsed into reaction chamber 120, at 630. Completing the pulsing of the second purging gas into reaction chamber 120 completes one cycle for a tantalum-zirconium dopant sequence. Then, it is determined whether the total number of cycles for the tantalum-zirconium dopant sequence has been reached to form the desired thickness for a dielectric film containing zirconium-doped TaO_(x), at 640.

If the total number of cycles to form the desired thickness has not been completed, the tantalum containing precursor is pulsed into reaction chamber, at 610, and the process continues. If the total number of cycles to form the desired thickness has been completed, the dielectric film containing zirconium-doped TaO_(x) can be annealed. The zirconium-doped TaO_(x) formed is amorphous and remains amorphous after annealing.

The thickness of a zirconium-doped TaO_(x) film is determined by a fixed growth rate for the pulsing periods and precursors used, set at a value such as N nm/cycle, dependent upon the tantalum precursor/zirconium dopant precursor mixture used. For a desired zirconium-doped TaO_(x) film thickness, t, in an application such as forming a gate dielectric of a MOS transistor, the ALD process is repeated for t/N total cycles. Once the t/N cycles have completed, no further ALD processing for zirconium-doped TaO_(x) is required. After forming the zirconium-doped TaO_(x), processing the device having the dielectric layer containing zirconium-doped TaO_(x) is completed, at 645, in a similar manner as for 570 of FIG. 5.

It can appreciated by those skilled in the art that the elements of a method for forming an atomic layer deposited zirconium-doped TaO_(x) film in the embodiment of FIG. 6 can be performed with various percentages for the zirconium containing precursor in the precursor mixture. In an embodiment, pulsing a zirconium containing precursor into the reaction chamber includes regulating the percentage of the zirconium containing precursor relative to the tantalum containing precursor to form a dielectric layer containing TaO_(x) doped with a predetermined percentage of the zirconium. In another embodiment, the zirconium-doped TaO_(x) layer may be amorphous. The atomic ratio of zirconium to the sum of zirconium and tantalum atoms may be regulated to select a dielectric constant in the range from about 8 to about 27. The selection of the dielectric constant may be conducted in a optimization, or trade-off, process with improving the current leakage characteristics of the film.

The embodiments described herein provide a process for growing a dielectric film having a wide range of useful equivalent oxide thickness, t_(eq), associated with a dielectric constant in the range from about 8 to about 27. This range of dielectric constants provides for a t_(eq) ranging from about 14% to about 48% of a given silicon dioxide thickness. Alternately, for an acceptable silicon dioxide thickness, an embodiment for a zirconium-doped tantalum oxide may be from two to seven times larger than the acceptable silicon dioxide thickness providing enhanced probability for reducing leakage current. Further, dielectric films of zirconium-doped TaO_(x) formed by atomic layer deposition can provide not only thin t_(eq) films, but also films with relatively low leakage current. Doping with zirconium yields a doped amorphous TaO_(x) with enhanced leakage current characteristics. Additionally, the novel process can be implemented to form transistors, capacitors, memory devices, and other electronic systems including information handling devices.

A transistor 700 as depicted in FIG. 7 may be constructed by forming a source region 720 and a drain region 730 in a silicon based substrate 710 where source and drain regions 720, 730 are separated by a body region 732. Body region 732 defines a channel having a channel length 734. A dielectric layer is disposed on substrate 710 formed as a layer containing zirconium-doped tantalum oxide on substrate 710 in a reaction chamber by atomic layer deposition. The resulting dielectric layer forms gate dielectric 740.

A gate 750 is formed over gate dielectric 740. Typically, forming gate 750 may include forming a polysilicon layer, though a metal gate may be formed in an alternative process. An interfacial layer 733 may form between body region 732 and gate dielectric 740. In an embodiment, interfacial layer 733 may be limited to a relatively small thickness compared to gate dielectric 740, or to a thickness significantly less than gate dielectric 740 as to be effectively eliminated. Forming the substrate, the source and drain regions, and the gate is performed using standard processes known to those skilled in the art. Additionally, the sequencing of the various elements of the process for forming a transistor is conducted with standard fabrication processes, also as known to those skilled in the art. In an embodiment, gate dielectric 740 may be realized as a gate insulator in a silicon CMOS transistor. Use of a gate dielectric containing zirconium-doped tantalum oxide is not limited to silicon based substrates, but may be used with a variety of semiconductor substrates.

FIG. 8 shows an embodiment of a configuration of a transistor 800 having an atomic layer deposited zirconium-doped TaO_(x) dielectric film. Transistor 800 includes a silicon based substrate 810 with a source 820 and a drain 830 separated by a body region 832. Body region 832 between source 820 and drain 830 defines a channel region having a channel length 834. Located above body region 832 is a stack 855 including a gate dielectric 840, a floating gate 852, a floating gate dielectric 842, and a control gate 850. Gate dielectric 840 includes a dielectric containing an atomic layer deposited zirconium-doped TaO_(x) dielectric film as described herein with the remaining elements of the transistor 800 formed using processes known to those skilled in the art. Alternately, both gate dielectric 840 and floating gate dielectric 842 may be formed as dielectric layers containing an atomic layer deposited zirconium-doped TaO_(x) dielectric film in various embodiments as described herein. An interfacial layer 833 may form between body region 832 and gate dielectric 840. In an embodiment, interfacial layer 833 may be limited to a relatively small thickness compared to gate dielectric 840, or to a thickness significantly less than gate dielectric 840 as to be effectively eliminated. In an embodiment, gate dielectric 840 forms a tunnel gate insulator and floating gate dielectric 842 forms an inter-gate insulator in flash memory devices, where gate dielectric 840 and/or floating gate dielectric 842 have an atomic layer deposited zirconium-doped tantalum oxide film. Use of a gate dielectric and/or floating gate dielectric containing an atomic layer deposited zirconium-doped tantalum oxide is not limited to silicon based substrates, but may be used with a variety of semiconductor substrates.

The embodiments of methods for forming dielectric layers containing an atomic layer deposited zirconium-doped TaO_(x) dielectric film may also be applied to forming capacitors in various integrated circuits, memory devices, and electronic systems. In an embodiment for forming a capacitor 900 illustrated in FIG. 9, a method includes forming a first conductive layer 910, forming a dielectric layer 920 containing an atomic layer deposited zirconium-doped TaO_(x) film on first conductive layer 910, and forming a second conductive layer 930 on dielectric layer 920. The dielectric layer containing zirconium-doped TaO_(x) may be formed using any of the embodiments described herein. ALD formation of the zirconium-doped TaO_(x) film allows the zirconium to be selectively doped into the TaO_(x) film within a predetermined range for the percentage of the zirconium in the film. An interfacial layer 915 may form between first conductive layer 910 and dielectric layer 920. In an embodiment, interfacial layer 915 may be limited to a relatively small thickness compared to dielectric layer 920, or to a thickness significantly less than dielectric layer 920 as to be effectively eliminated. Embodiments for dielectric layer 920 containing an atomic layer deposited zirconium-doped TaO_(x) in a capacitor includes, but is not limited to, dielectrics in DRAM capacitors and as dielectrics in capacitors in analog, radio frequency (RF), and mixed signal integrated circuits.

Various embodiments for a dielectric film containing atomic layer deposited zirconium-doped tantalum oxide provide for enhanced device performance by providing devices with reduced leakage current. Further improvements in leakage current characteristics may be attained by forming one or more layers of an atomic layer deposited zirconium-doped tantalum oxide in a nanolaminate structure with other metal oxides such as TaO_(x) and ZrO_(x). The transition from one layer of the nanolaminate to another layer of the nanolaminate provides further disruption to a tendency for an ordered structure in the nanolaminate stack. The term “nanolaminate” means a composite film of ultra thin layers of two or more materials in a layered stack, where the layers are alternating layers of materials of the composite film. Typically, each layer in a nanolaminate has a thickness of an order of magnitude in the nanometer range. Further, each individual material layer of the nanolaminate can have a thickness as low as a monolayer of the material or as high as 20 nanometers. A TaO_(x)/ZrO_(x)/zirconium-doped TaO_(x) nanolaminate contains alternating layers of TaO_(x) and ZrO_(x) and zirconium-doped TaO_(x).

FIG. 10 depicts a nanolaminate structure 1000 for an embodiment of a dielectric structure including an atomic layer deposited zirconium-doped TaO_(x) dielectric film. Nanolaminate structure 1000 includes a plurality of layers 1005-1, 1005-2 to 1005-N, where at least one layer contains an atomic layer deposited zirconium-doped TaO_(x) dielectric film. The other layers may be other metal oxides such as TaO_(x) and ZrO_(x). The sequencing of the layers depends on the application. The effective dielectric constant associated with nanolaminate structure 1000 is that attributable to N capacitors in series, where each capacitor has a thickness defined by the thickness of the corresponding layer. By selecting each thickness and the composition of each a nanolaminate structure can be engineered to have a predetermined dielectric constant. Embodiments for structures such as nanolaminate structure 1000 may be used as nanolaminate dielectrics in NROM flash memory devices as well as other integrated circuits.

Transistors, capacitors, and other devices having dielectric films containing atomic layer deposited zirconium-doped TaO_(x) formed by the methods described above may be implemented into memory devices and electronic systems including information handling devices. Embodiments of these information handling devices may include wireless systems, telecommunication systems, and computers. Further, embodiments of electronic devices having dielectric films containing atomic layer deposited zirconium-doped tantalum oxide may be realized as integrated circuits.

FIG. 11 illustrates a diagram for an electronic system 1100 having one or more devices with an embodiment for a dielectric layer containing atomic layer deposited zirconium-doped TaO_(x). Electronic system 1100 includes a controller 1105, a bus 1115, and an electronic device 1125, where bus 1115 provides electrical conductivity between controller 1105 and electronic device 1125. In various embodiments, controller 1005 and/or electronic device 1125 include an embodiment for a dielectric layer containing atomic layer deposited zirconium-doped TaO_(x) as previously discussed herein. Electronic system 1100 may include, but is not limited to, information handling devices, wireless systems, telecommunication systems, fiber optic systems, electro-optic systems, and computers.

FIG. 12 depicts a diagram of an embodiment of a system 1200 having a controller 1205 and a memory 1225. Controller 1205 and/or memory 1225 may include a dielectric layer having an atomic layer deposited zirconium-doped TaO_(x). System 1200 also includes an electronic apparatus 1235, and a bus 1215, where bus 1215 provides electrical conductivity between controller 1205 and electronic apparatus 1235, and between controller 1205 and memory 1225. Bus 1215 may include an address, a data bus, and a control bus, each independently configured. Alternately, bus 1215 may use common conductive lines for providing address, data, and/or control, the use of which is regulated by controller 1205. In an embodiment, electronic apparatus 1235 may be additional memory configured similar as memory 1225. An embodiment may include an additional peripheral device or devices 1245 coupled to bus 1215. In an embodiment controller 1205 is a processor. Any of controller 1205, memory 1225, bus 1215, electronic apparatus 1235, and peripheral device devices 1245 may include a dielectric layer having an atomic layer deposited zirconium-doped TaO_(x). System 1200 may include, but is not limited to, information handling devices, telecommunication systems, and computers.

Peripheral devices 1245 may include displays, additional storage memory, or other control devices that may operate in conjunction with controller 1205. Alternately, peripheral devices 1245 may include displays, additional storage memory, or other control devices that may operate in conjunction with controller 1205 and/or memory 1225.

Memory 1225 may be realized as a memory device containing an atomic layer deposited zirconium-doped TaO_(x) dielectric layer. It will be understood that embodiments are equally applicable to any size and type of memory circuit and are not intended to be limited to a particular type of memory device. Memory types include a DRAM, SRAM (Static Random Access Memory) or Flash memories. Additionally, the DRAM could be a synchronous DRAM commonly referred to as SGRAM (Synchronous Graphics Random Access Memory), SDRAM (Synchronous Dynamic Random Access Memory), SDRAM II, and DDR SDRAM (Double Data Rate SDRAM), as well as Synchlink or Rambus DRAMs and other emerging DRAM technologies.

Zirconium-doped tantalum oxide films formed by atomic layer deposition processed in relatively low temperatures can be amorphous and possess smooth surfaces. Such zirconium-doped tantalum oxide films can provide enhanced electrical properties due to their smoother surface resulting in reduced leakage current. Additionally, zirconium-doped tantalum oxide films by atomic layer deposition may also provide reduced leakage current while providing an increased dielectric constant as compared with undoped tantalum oxide and pure zirconium oxide layers. Additionally, such dielectric layers provide a significantly thicker physical thickness than a silicon oxide layer having the same equivalent oxide thickness, where the increased thickness would also reduce leakage current. These properties of layers containing atomic layer deposited zirconium-doped tantalum oxide films allow for application as dielectric layers in numerous electronic devices and systems.

Capacitors, transistors, higher level ICs or devices including memory devices, and electronic systems are constructed utilizing the novel process for forming a dielectric film having an ultra thin equivalent oxide thickness, t_(eq). Gate dielectric layers or films containing atomic layer deposited zirconium-doped tantalum oxide are formed having a dielectric constant (κ) substantially higher than that of silicon oxide, such that these dielectric films are capable of a t_(eq) thinner than SiO₂ gate dielectrics of the same physical thickness. Alternately, the high dielectric constant relative to silicon dioxide allows the use of much larger physical thickness of these high-κ dielectric materials for the same t_(eq) of SiO₂. Forming the relatively larger thickness aids in processing gate dielectrics and other dielectric layers in electronic devices and systems.

Although specific embodiments have been illustrated and described herein, it will be appreciated by those of ordinary skill in the art that any arrangement that is calculated to achieve the same purpose may be substituted for the specific embodiments shown. This application is intended to cover any adaptations or variations of embodiments of the present invention. It is to be understood that the above description is intended to be illustrative, and not restrictive, and that the phraseology or terminology employed herein is for the purpose of description and not of limitation. Combinations of the above embodiments and other embodiments will be apparent to those of skill in the art upon studying the above description. The scope of the present invention includes any other applications in which embodiment of the above structures and fabrication methods are used. The scope of the embodiments of the present invention should be determined with reference to the appended claims, along with the full scope of equivalents to which such claims are entitled. 

1. A method comprising: forming tantalum oxide on a substrate using a self-limiting deposition process; doping the tantalum oxide with zirconium at different times during the self-limiting deposition process such that a zirconium-doped tantalum oxide is formed; and controlling the doping with zirconium to an amount such that the zirconium-doped tantalum oxide has a structure that does not differ significantly from an undoped tantalum oxide structure.
 2. The method of claim 1, wherein doping the tantalum oxide with zirconium includes doping as elemental zirconium.
 3. The method of claim 1, wherein doping the tantalum oxide with zirconium includes doping as zirconium oxide.
 4. The method of claim 1, wherein forming zirconium-doped tantalum oxide includes forming an amorphous zirconium-doped tantalum oxide.
 5. The method of claim 1, wherein forming the tantalum oxide including doping the tantalum oxide with zirconium is conducted at temperatures between about 250° C. and about 325° C.
 6. The method of claim 1, wherein forming tantalum oxide on a substrate includes forming the tantalum oxide on a silicon substrate.
 7. The method of claim 6, wherein forming the tantalum oxide including doping the tantalum oxide with zirconium is conducted at temperatures such that a silicon oxide interface is formed between the zirconium-doped tantalum oxide and the silicon substrate.
 8. The method of claim 1, wherein the method includes providing a tantalum containing precursor directed to the substrate and providing a zirconium containing precursor directed to the substrate such that these precursors are directed to the substrate at non-overlapping periods.
 9. The method of claim 8, wherein the method includes forming the tantalum oxide and doping the tantalum oxide with zirconium using precursors without chlorine.
 10. The method of claim 9, wherein using precursors without chlorine includes using ZrI₄ as a zirconium-containing precursor.
 11. The method of claim 1, wherein the method includes forming the zirconium-doped tantalum oxide as a gate insulator in a transistor.
 12. The method of claim 8, wherein the method includes forming the zirconium-doped tantalum oxide as a gate insulator in a CMOS device.
 13. The method of claim 1, wherein the method includes forming the zirconium-doped tantalum oxide as a dielectric between two electrodes of a capacitor.
 14. The method of claim 1, wherein the method includes forming the zirconium-doped tantalum oxide as a gate insulator of a transistor in a memory array of a memory device.
 15. The method of claim 1, wherein the method includes forming the zirconium-doped tantalum within a multi-component dielectric.
 16. The method of claim 15, wherein forming the multi-component dielectric includes forming a nanolaminate dielectric.
 17. The method of claim 16, wherein forming the nanolaminate dielectric includes forming the nanolaminate dielectric in a memory array of a NROM flash memory device.
 18. The method of claim 1, wherein doping the tantalum oxide with zirconium includes pulsing a zirconium containing precursor during a portion of the time that a tantalum containing precursor is being pulsed.
 19. The method of claim 1, wherein forming the zirconium-doped tantalum oxide includes performing a number of cycles of the self-limiting deposition process containing a number of tantalum processing sequences and a number of zirconium processing sequences, the number of tantalum processing sequences greater than the number of zirconium processing sequences.
 20. The method of claim 19, wherein the number of zirconium processing sequences is performed as substitution for a portion of the tantalum sequences in the number of cycles. 